Magnetic material, permanent magnet, rotary electrical machine, and vehicle

ABSTRACT

An magnetic material is a magnetic material expressed by a composition formula: (R1-xYx)aMbTcAd, which includes a main phase consisting of a ThMn12 type crystal phase. 30 atomic percent or more of the element M in the composition formula is Fe.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a Continuation-In-Part of application Ser. No.15/440,057 filed Feb. 23, 2017; the entire contents of which areincorporated herein by reference.

This application is based upon and claims the benefit of priority fromJapanese Patent Applications No. 2016-163797 filed on Aug. 24, 2016, No.2017-018622 filed on Feb. 3, 2017, and No. 2017-135371 filed on Jul. 11,2017; the entire contents of all of which are incorporated herein byreference.

FIELD

Embodiments described herein generally relate to a magnetic material, apermanent magnet, a rotary electrical machine, and a vehicle.

BACKGROUND

Permanent magnets are used for products in a wide field including rotaryelectrical machines such as a motor and a power generator, electricalapparatuses such as a speaker and a measuring device, and vehicles suchas an automobile and a railroad vehicle. In recent years, reduction insize of the above-described products has been demanded, andhigh-performance permanent magnets with high magnetization and highcoercive force have been desired.

As examples of high-performance permanent magnets, there can be citedrare-earth magnets such as Sm—Co based magnets and Nd—Fe—B basedmagnets, for example. In these magnets, Fe and Co contribute to increasein saturation magnetization. Further, these magnets contain rare-earthelements such as Nd and Sm, which brings about a large magneticanisotropy which is derived from a behavior of 4f electrons of therare-earth elements in a crystal field. Consequently, it is possible toobtain a large coercive force.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a diagram illustrating an example of an X-ray diffractionpattern of a magnetic material expressed by a composition formula:(Sm_(0.82)Y_(0.18))_(7.7)(Fe_(0.70)Co_(0.30))_(88.4)Ti_(3.9).

FIG. 2 is a diagram illustrating an example of an X-ray diffractionpattern of a magnetic material expressed by a composition formula:(Sm_(0.68)Zr_(0.32))_(7.8)(Fe_(0.70)Co_(0.30))_(88.2)Ti_(4.0).

FIG. 3 is an example of an X-ray diffraction pattern having a peakcorresponding to a Nd₃(Fe, Ti)₂₉ type crystal phase.

FIG. 4 is a diagram illustrating a permanent magnet motor.

FIG. 5 is a diagram illustrating a variable magnetic flux motor.

FIG. 6 is a diagram illustrating a power generator.

FIG. 7 is a schematic diagram illustrating a configuration example of arailroad vehicle.

FIG. 8 is a schematic diagram illustrating a configuration example of anautomobile.

DETAILED DESCRIPTION

A problem to be solved by the present invention is to increasesaturation magnetization of the magnetic material.

A magnetic material of an embodiment is expressed by a compositionformula 1: (R_(1-x)Y_(x))_(a)M_(b)T_(c) (in the formula, R is arare-earth element of one kind or more, T is at least one elementselected from the group consisting of Ti, V, Nb, Ta, Mo, and W, M is Feor Fe and Co, x is a number satisfying 0.01≤x≤0.8, a is a numbersatisfying 4≤a≤20 atomic percent, b is a number satisfying b=100−a−catomic percent, and c is a number satisfying 0<c<7 atomic percent). Themagnetic material includes a main phase formed of a ThMn₁₂ type crystalphase. 30 atomic percent or more of the element M in the compositionformula 1 is Fe.

Hereinafter, embodiments will be described while referring to thedrawings. The drawings are schematically illustrated, and, for example,a relationship between a thickness and a plane dimension, a ratio ofthicknesses of respective layers, and the like, are sometimes differentfrom actual ones. Further, in the embodiments, substantially the samecomponents are denoted by the same reference numerals, and explanationthereof will be omitted.

First Embodiment

A magnetic material of the present embodiment contains a rare-earthelement and an element M (M is Fe or Fe and Co). The magnetic materialincludes a metal structure having a crystal phase as a main phase, andby increasing a concentration of the element M in the main phase, it ispossible to improve saturation magnetization. The main phase has thehighest volume occupancy ratio among respective crystal phases and anamorphous phase in the magnetic material.

Examples of a crystal phase containing the element M of highconcentration include a ThMn₁₂ type crystal phase. The ThMn₁₂ typecrystal phase has a crystal structure of tetragonal system. The magneticmaterial having the ThMn₁₂ type crystal phase as its main phase has ahigh concentration of the element M to lead precipitation of an α-(Fe,Co) phase. If a hetero-phase such as the α-(Fe, Co) phase precipitates,the concentration of the element M in the main phase reduces, whichcauses reduction in saturation magnetization of the main phase. Further,the precipitation of the α-(Fe, Co) phase causes reduction in coerciveforce of the permanent magnet. Accordingly, in the magnetic material ofthe present embodiment, the reduction in the saturation magnetization issuppressed by reducing the α-(Fe, Co) phase to improve the concentrationof the element M in the main phase, while forming a stabilized ThMn₁₂type crystal phase by controlling concentrations of respective elementscontained in the main phase.

The magnetic material of the present embodiment has a compositionexpressed by a composition formula 1: (R_(1-x)Y_(x))_(a)M_(b)T_(c) (inthe formula, R is a rare-earth element of one kind or more, T is atleast one element selected from the group consisting of Ti, V, Nb, Ta,Mo, and W, M is Fe or Fe and Co, x is a number satisfying 0.01≤x≤0.8, ais a number satisfying 4≤a≤20 atomic percent, b is a number satisfyingb=100−a−c atomic percent, and c is a number satisfying 0<c<7 atomicpercent). The magnetic material may also contain inevitable impurities.

Yttrium (Y) is an element effective for stabilization of the ThMn₁₂ typecrystal phase. Specifically, the element Y can mainly increase stabilityof the ThMn₁₂ type crystal phase through reduction in a crystal latticecaused when it is replaced with the element R in the main phase, and thelike. When an addition amount of the element Y is too small, it is notpossible to sufficiently achieve an effect of increasing the stabilityof the ThMn₁₂ type crystal phase. When the addition amount of Y is toolarge, an anisotropic magnetic field of the magnetic materialsignificantly lowers. It is preferable that x is a number satisfying0.01≤x≤0.8, it is more preferable that x is a number satisfying0.05≤x≤0.5, and it is still more preferable that x is a numbersatisfying 0.1≤x≤0.4.

50 atomic percent or less of the element Y may be replaced with at leastone element selected from the group consisting of zirconium (Zr) andhafnium (Hf). The element Zr and the element Hf are elements capable ofrealizing exhibition of large coercive force in a composition of high Feconcentration. When the element Y is replaced with the element Zr andthe element Hf, it is possible to increase the coercive force.

The element R is a rare-earth element, and an element capable ofproviding large magnetic anisotropy to the magnetic material, and givinghigh coercive force to a permanent magnet. The element R is, concretely,at least one element selected from the group consisting of lanthanum(La), cerium (Ce), praseodymium (Pr), neodymium (Nd), promethium (Pr),samarium (Sm), europium (Eu), gadolinium (Gd), terbium (Tb), dysprosium(Dy), holmium (Ho), erbium (Er), thulium (Tm), ytterbium (Yb), andlutetium (Lu), and it is preferable to use Sm, in particular. Forexample, when a plurality of elements including Sm are used as theelement R, by setting the Sm concentration to 50 atomic percent or moreof all of the elements capable of being applied as the element R, it ispossible to increase the performance, for example, the coercive force ofthe magnetic material.

The concentration a of the element R and the element Y is preferably anumber satisfying 4≤a≤20 atomic percent, for example. When theconcentration a is less than 4 atomic percent, a large amount of theα-(Fe, Co) phase precipitates, which reduces the coercive force. Whenthe concentration a exceeds 20 atomic percent, a gain boundary phaseincreases, which reduces the saturation magnetization. The concentrationa of the element R and the element Y is more preferably a numbersatisfying 5≤a≤18 atomic percent, and still more preferably a numbersatisfying 7≤a≤15 atomic percent.

The element M is Fe or Fe and Co, and is an element responsible for highsaturation magnetization of the magnetic material. When compared betweenFe and Co, Fe causes higher magnetization, so that Fe is an essentialelement, and in the magnet of the present embodiment, 30 atomic percentor more of the element M is Fe. By making the element M contain Co, theCurie temperature of the magnetic material increases, resulting in thatthe reduction in the saturation magnetization in a high-temperatureregion can be suppressed. Further, by adding a small amount of Co, thesaturation magnetization can be further increased, when compared to acase where Fe is solely used. On the other hand, if a Co ratio isincreased, the reduction in the anisotropic magnetic field is caused.Further, if the Co ratio is too high, the reduction in the saturationmagnetization is also caused. For this reason, by appropriatelycontrolling the ratio between Fe and Co, it is possible tosimultaneously realize high saturation magnetization, high anisotropicmagnetic field, and high Curie temperature. When M in the compositionformula 1 is represented as (Fe_(1-y)Co_(y)), a desirable value of y is0.01≤x<0.7, the value is more preferably 0.01≤y<0.5, and is still morepreferably 0.01≤y≤0.3. 20 atomic percent or less of the element M may bereplaced with at least one element selected from the group consisting ofaluminum (Al), silicon (Si), chromium (Cr), manganese (Mn), nickel (Ni),copper (Cu), and gallium (Ga). The above-described elements contributeto growth of crystal grains which form the main phase, for example.

The element T is at least one element selected from the group consistingof titanium (Ti), vanadium (V), niobium (Nb), tantalum (Ta), molybdenum(Mo), and tungsten (W), for example. By adding the element T, it ispossible to stabilize the ThMn₁₂ type crystal phase. However, by theintroduction of the element T, the concentration of the element Mreduces, resulting in that the saturation magnetization of the magneticmaterial easily reduces. In order to increase the concentration of theelement M, it is only required to reduce the addition amount of T, but,in such a case, the stability of the ThMn₁₂ type crystal phase is lost,and the α-(Fe, Co) phase precipitates, which leads to reduction in thecoercive force of the magnetic material. The addition amount c of theelement T is preferably a number satisfying 0<c<7 atomic percent.Consequently, it is possible to stabilize the ThMn₁₂ type crystal phasewhile suppressing the precipitation of the α-(Fe, Co) phase. It is morepreferable that 50 atomic percent or more of the element T is Ti or Nb.By using Ti or Nb, even if the content of the element T is reduced, itis possible to greatly reduce the precipitation amount of the α-(Fe, Co)phase while stabilizing the ThMn₁₂ type crystal phase.

In order to increase the saturation magnetization of the magneticmaterial, it is preferably to reduce the amount of the element T.However, the reduction of the amount of the element T may cause theprecipitation of a Nd₃(Fe, Ti)₂₉ type crystal phase and thus reductionof the saturation magnetization. In order to suppress the precipitationof the Nd₃(Fe, Ti)₂₉ type crystal phase with the reduction of the amountof the element T, it is effective to increase the amount of Y. Thisenables an increase of the saturation magnetization. If the additionamount c of the element T is a number satisfying 0<c<4.5 atomic percent,x is preferably a number satisfying 0.1<x<0.6. If c is a numbersatisfying 1.5<c<4 atomic percent, x is preferably a number satisfying0.15<x≤0.55. If c is a number satisfying 3<c≤3.8 atomic percent, x ispreferably a number satisfying 0.3<x≤0.5.

The magnetic material of the present embodiment may further contain anelement A. At this time, a composition of the magnetic material isexpressed by a composition formula 2: (R_(1-x)Y_(x))_(a)M_(b)T_(c)A_(d)(in the formula, R is a rare-earth element of one kind or more, T is atleast one element selected from the group consisting of Ti, V, Nb, Ta,Mo, and W, M is Fe or Fe and Co, A is at least one element selected fromthe group consisting of N, C, B, H, and P, x is a number satisfying0.01≤x≤0.8, a is a number satisfying 4≤a≤20 atomic percent, c is anumber satisfying 0<c<7 atomic percent, b is a number satisfyingb=100−a−c−d atomic percent, and d is a number satisfying 0<d≤18 atomicpercent).

The element A is at least one element selected from the group consistingof nitrogen (N), carbon (C), boron (B), hydrogen (H), and phosphorus(P). The element A has a function of entering a crystal lattice of theThMn₁₂ type crystal phase to cause at least one of enlargement of thecrystal lattice and change in electronic structure, for example.Consequently, it is possible to change the Curie temperature, themagnetic anisotropy, and the saturation magnetization. The element Adoes not always have to be added, except for inevitable impurities.

When 50 atomic percent or more of the element R is Sm (when a maincomponent of the element R is Sm), the magnetic anisotropy of the ThMn₁₂type crystal phase changes from a c axis direction to a directionoriented in a plane perpendicular to the c axis due to the entrance ofthe element A, which reduces the coercive force. For this reason, it ispreferable that the element A is not added except for inevitableimpurities. On the contrary, when 50 atomic percent or more of theelement R is at least one element selected from the group consisting ofCe, Pr, Nd, Tb, and Dy (when the main component of the element R is atleast one element selected from the group consisting of Ce, Pr, Nd, Tb,and Dy), the magnetic anisotropy of the ThMn₁₂ type crystal phasechanges from the direction oriented in the plane perpendicular to the caxis to the c axis direction due to the entrance of the element A, whichenables to increase the coercive force. For this reason, the element Ais preferably added. When the element A is added, the concentration d ofthe element A is preferably a number satisfying 0<d≤18 atomic percent.When the concentration d exceeds 18 atomic percent, the stability of theThMn₁₂ type crystal phase reduces. The concentration d of the element Ais more preferably a number satisfying 0<d≤14 atomic percent.

FIG. 1 is a diagram illustrating an example of an X-ray diffractionpattern of a magnetic material expressed by a composition formula:(Sm_(0.82)Y_(0.18))_(7.7)(Fe_(0.70)Co_(0.30))_(88.4)Ti_(3.9), and FIG. 2is a diagram illustrating an example of an X-ray diffraction pattern ofa magnetic material expressed by a composition formula:(Sm_(0.68)Zr_(0.32))_(7.8)(Fe_(0.70)Co_(0.30))_(88.2)Ti_(4.0). The X-raydiffraction patterns illustrated in FIG. 1 and FIG. 2 can be obtained byperforming X-ray diffraction (XRD) measurement on the magneticmaterials. From the X-ray diffraction patterns illustrated in FIG. 1 andFIG. 2, it can be understood that each of the magnetic materialsincludes a metal structure having a ThMn₁₂ type crystal phase as itsmain phase.

A maximum value I_(α-(Fe,Co)) of a peak intensity brought by an α-(Fe,Co) phase in the X-ray diffraction pattern illustrated in FIG. 1, issmaller than a maximum value I_(α-(Fe, Co)) of a peak intensity broughtby an α-(Fe, Co) phase in the X-ray diffraction pattern illustrated inFIG. 2. This indicates that the magnetic material of the presentembodiment has a small precipitation amount of the α-(Fe, Co) phase. Inthe X-ray diffraction pattern of the magnetic material of the presentembodiment, a ratio of a maximum value I_(α-(Fe, Co)) of a peakintensity brought by the α-(Fe, Co) phase to a sum of a maximum valueI_(ThMn12) of a peak intensity brought by the ThMn₁₂ type crystal phaseand the maximum value I_(α-(Fe, Co)) of the peak intensity brought bythe α-(Fe, Co) phase (I_(α-(Fe, Co))/(I_(α-(Fe, Co))+I_(ThMn12))) ispreferably less than 0.20, more preferably less than 0.15, and stillmore preferably less than 0.10.

FIG. 3 is an example of an X-ray diffraction pattern having a peakcorresponding to the Nd₃(Fe, Ti)₂₉ type crystal phase. FIG. 3 shows thatthe precipitation of the Nd₃(Fe, Ti)₂₉ type crystal phase is determinedby a peak at diffraction angles 2θ of 39 to 40 degrees of the X-raydiffraction pattern. In the X-ray diffraction pattern, the precipitationamount of the Nd₃(Fe, Ti)₂₉ type crystal phase is defined by a ratio ofa maximum value β₃₋₂₉ of a peak intensity brought by the Nd₃(Fe, Ti)₂₉type crystal phase to a sum of a maximum value I_(ThMn12) of a peakintensity brought by the ThMn₁₂ type crystal phase and the maximum valueI₃₋₂₉ of the peak intensity brought by the Nd₃(Fe, Ti)₂₉ type crystalphase (I₃₋₂₉/(I₃₋₂₉+I_(TMn12))). I₃₋₂₉/(I₃₋₂₉+I_(ThMn12)) is preferably0.070 or less, more preferably less than 0.050, and still morepreferably less than 0.040.

In the magnetic material of the present embodiment, as the concentrationof the element M in the main phase becomes high, the saturationmagnetization of the magnetic material can be increased. Theconcentration of the element M in the main phase of the magneticmaterial is preferably 85 atomic percent or more, more preferably 87.4atomic percent or more, still more preferably 87.6 atomic percent ormore, and yet more preferably 88.0 atomic percent or more of the totalamount of the elements except for the element A (the element R, theelement Y, the element M, and the element T) in the main phase.

In the magnetic material of the present embodiment, by setting theconcentration of the element M in the main phase to 87.4 atomic percentor more of the total amount of the elements except for the element A(the element R, the element Y, the element M, and the element T) in themain phase. Therefore, it is possible to provide the magnetic materialhaving the saturation magnetization higher than the conventionalsaturation magnetization. The saturation magnetization of the entiremagnetic material is preferably higher than 1.48 T, and more preferably1.52 T or higher, for example. Further, the saturation magnetization ofthe main phase except for the contribution of saturation magnetizationof the α-(Fe, Co) phase is preferably higher than 1.41 T, and morepreferably 1.50 T or higher, for example. Magnetic physical propertiessuch as the saturation magnetization are calculated by using a vibratingsample magnetometer (VSM), for example.

The composition of the magnetic material is measured through, forexample, ICP-AES (Inductively Coupled Plasma-Atomic EmissionSpectroscopy), SEM-EDX (Scanning Electron Microscope-Energy DispersiveX-ray Spectroscopy), TEM-EDX (Transmission Electron Microscope-EnergyDispersive X-ray Spectroscopy), or the like. The volume ratios of therespective phases are determined in a comprehensive manner by using bothof observation with an electron microscope or an optical microscope, andthe X-ray diffraction or the like.

The concentrations of the respective elements of the main phase aremeasured by using the SEM-EDX, for example. For example, the main phasecan be specified by an observation image obtained through the SEM and amapping image of each element of a measurement sample of the magneticmaterial obtained through the SEM-EDX.

Next, an example of manufacturing method of the magnetic material of thepresent embodiment will be described. First, an alloy containingpredetermined elements required for the magnetic material ismanufactured. The alloy can be manufactured by using, for example, anarc melting method, a high-frequency melting method, a metal moldcasting method, a mechanical alloying method, a mechanical grindingmethod, a gas atomizing method, a reduction diffusion method, or thelike. When the α-(Fe, Co) phase is generated in the manufactured alloy,this leads to reduction in the coercive force of the permanent magnetmanufactured from this alloy.

Further, the above-described alloy is melted to be subjected to rapidcooling. This enables to reduce the precipitation amount of the α-(Fe,Co) phase. The melted alloy is subjected to rapid cooling by using astrip cast method, for example. In the strip cast method, the alloymolten metal is tiltingly injected to a chill roll, to therebymanufacture an alloy thin strip. At this time, by controlling a rotationspeed of the roll, a cooling rate of the molten metal can be controlled.The roll may be one of either a single-roll type or a twin-roll type.

Heat treatment may also be performed on the above-described alloy thinstrip. This enables to homogenize the material. For example, heating isperformed at 800 to 1300° C. for 2 to 120 hours. Consequently, itbecomes possible to increase the stability of the ThMn₁₂ type crystalphase to further improve both properties of the saturation magnetizationand the anisotropic magnetic field.

It is also possible to make the element A enter the above-describedalloy thin strip. It is preferable that the alloy is pulverized into apowder before the process of making the element A enter the alloy. Whenthe element A is nitrogen, by heating the alloy thin strip for 1 to 100hours in an atmosphere of nitrogen gas, ammonia gas, or the like ofabout 0.1 to 100 atmospheric pressure, in a temperature range of 200 to700° C., it is possible to nitride the alloy thin strip to make theelement N enter the alloy thin strip. When the element A is carbon, byheating the alloy thin strip for 1 to 100 hours in an atmosphere ofC₂H₂, CH₄, C₃H₈, or Co gas of about 0.1 to 100 atmospheric pressure orthermal decomposition gas of methanol in a temperature range of 300 to900° C., it is possible to carbonize the alloy thin strip to make theelement C enter the alloy thin strip. When the element A is hydrogen, byheating the alloy thin strip for 1 to 100 hours in an atmosphere ofhydrogen gas, ammonia gas, or the like of about 0.1 to 100 atmosphericpressure, in a temperature range of 200 to 700° C., it is possible tohydrogenate the alloy thin strip to make the element H enter the alloythin strip. When the element A is boron, by making a raw materialcontain boron when manufacturing the alloy, it is possible to make boronto be contained in the alloy thin strip. When the element A isphosphorus, by phosphorizing the alloy thin strip, it is possible tomake the element P enter the alloy thin strip.

The magnetic material is manufactured through the above-describedprocess. Further, the permanent magnet is manufactured by using theaforementioned magnetic material. For example, by pulverizing theaforementioned magnetic material and then performing heat treatment suchas sintering, a sintered magnet including a sintered compact of theaforementioned magnetic material is manufactured. Further, bypulverizing the aforementioned magnetic material and then performingsolidification using a resin or the like, a bond magnet including theaforementioned magnetic material is manufactured.

Second Embodiment

The permanent magnet including the sintered compact of the magneticmaterial of the first embodiment can be used for various motors andpower generators. Further, it is possible to use the permanent magnet asa stationary magnet or a variable magnet of a variable magnetic fluxmotor or a variable magnetic flux power generator. Various motors andpower generators are formed by using the permanent magnet of the firstembodiment. When the permanent magnet of the first embodiment is appliedto a variable magnetic flux motor, techniques disclosed in JapanesePatent Application Laid-open No. 2008-29148 or Japanese PatentApplication Laid-open No. 2008-43172 can be applied to a configurationand a drive system of the variable magnetic flux motor.

Next, a motor and a power generator including the above-describedpermanent magnet will be described with reference to the drawings. FIG.4 is a diagram illustrating a permanent magnet motor. In a permanentmagnet motor 1 illustrated in FIG. 4, a rotor 3 is disposed in a stator2. In an iron core 4 of the rotor 3, permanent magnets 5 being thepermanent magnets of the first embodiment are disposed. By using thepermanent magnets of the first embodiment, high efficiency, reduction insize, cost reduction and the like of the permanent magnet motor 1 can beachieved based on properties and the like of the respective permanentmagnets.

FIG. 5 is a diagram illustrating a variable magnetic flux motor. In avariable magnetic flux motor 11 illustrated in FIG. 5, a rotor 13 isdisposed in a stator 12. In an iron core 14 of the rotor 13, thepermanent magnet of the first embodiment is disposed as stationarymagnets 15 and variable magnets 16. A magnetic flux density (magneticflux amount) of the variable magnets 16 is variable. A magnetizationdirection of the variable magnets 16 is orthogonal to a Q-axisdirection, and thus the magnets are not affected by a Q-axis current,and can be magnetized by a D-axis current. A magnetization winding (notillustrated) is provided on the rotor 13. It is structured such that bypassing a current through the magnetization winding from a magnetizingcircuit, a magnetic field thereof operates directly on the variablemagnets 16.

According to the permanent magnet of the first embodiment, it ispossible to obtain the coercive force suitable for the stationarymagnets 15. When the permanent magnet of the first embodiment is appliedto the variable magnets 16, it is only required to control the coerciveforce, for example, to fall within a range of not less than 100 kA/m normore than 500 kA/m by changing the manufacturing conditions. In thevariable magnetic flux motor 11 illustrated in FIG. 5, the permanentmagnet of the first embodiment can be used for both of the stationarymagnets 15 and the variable magnets 16, but, it is also possible to usethe permanent magnet of the first embodiment for either of the magnets.The variable magnetic flux motor 11 is capable of outputting a largetorque from a small device size, and thus is preferred for a motor of ahybrid vehicle, electric vehicle, or the like required to have highoutput power and small size of the motor.

FIG. 6 illustrates a power generator. A power generator 21 illustratedin FIG. 6 includes a stator 22 using the above-described permanentmagnet. A rotor 23 disposed inside the stator 22 is connected via ashaft 25 to a turbine 24 provided at one end of the power generator 21.The turbine 24 is rotated by an externally supplied fluid, for example.Instead of the turbine 24 rotated by the fluid, the shaft 25 can also berotated by transmitting dynamic rotation such as regenerative energy ofan automobile. To the stator 22 and the rotor 23, various publicly-knownconfigurations can be adopted.

The shaft 25 is in contact with a commutator (not illustrated) disposedon the opposite side of the turbine 24 with respect to the rotor 23, andelectromotive force generated by rotations of the rotor 23 is increasedin voltage to a system voltage and transmitted as output of the powergenerator 21 via isolated phase buses and a main transformer (notillustrated). The power generator 21 may be either of an ordinary powergenerator and a variable magnetic flux power generator. A staticelectricity from the turbine 24 or charges by an axial currentaccompanying power generation occur on the rotor 23. For this reason,the power generator 21 includes a brush 26 for discharging the chargesof the rotor 23.

An use of the above-described permanent magnet to the power generatorenable effects such as high efficiency, reduction in size, and costreduction.

The above-described rotary electrical machine may be mounted on arailroad vehicle (one example of vehicle) used in railway traffic, forexample. FIG. 7 is a diagram illustrating one example of a railroadvehicle 100 including a rotary electrical machine 101. As the rotaryelectrical machine 101, the motor in FIG. 4 or FIG. 5, the powergenerator in FIG. 6 described above, or the like. When theabove-described rotary electrical machine is mounted as the rotaryelectrical machine 101, the rotary electrical machine 101 may be used asan electric motor (motor) which outputs a driving force by utilizingelectric power supplied from a power transmission line or electric powersupplied from a secondary battery mounted on the railroad vehicle 100,for example, or it may also be used as a power generator (generator)which converts kinetic energy into electric power and supplies theelectric power to various loads in the railroad vehicle 100. Byutilizing a highly efficient rotary electric machine such as the rotaryelectrical machine of the embodiment, it is possible to make therailroad vehicle travel while saving energy.

The aforementioned rotary electrical machine may also be mounted on anautomobile (another example of vehicle) such as a hybrid vehicle or anelectric vehicle. FIG. 8 is a diagram illustrating one example of anautomobile 200 including a rotary electrical machine 201. As the rotaryelectrical machine 201, the motor in FIG. 4 or FIG. 5, the powergenerator in FIG. 6 described above, or the like. When theabove-described rotary electrical machine is mounted as the rotaryelectrical machine 201, the rotary electrical machine 201 may be used asan electric motor which outputs a driving force of the automobile 200,or it may also be used as a power generator which converts kineticenergy at the time of traveling the automobile 200 into electric power.

EXAMPLES Examples 1 to 38

Appropriate amounts of raw materials were weighed to produce alloys byusing the arc melting method. Next, each of the alloys was melted, andthe obtained molten metal was subjected to rapid cooling by using thestrip cast method, to thereby produce an alloy thin strip. Theabove-described alloy thin strips were heated for 4 hours at 1100° C.under an Ar atmosphere. Thereafter, compositions of the alloy thinstrips after being subjected to the heating were analyzed by using theICP-AES. The compositions of the magnetic materials obtained by usingthe ICP-AES are presented in Table 1.

Next, each of the alloy thin strips was pulverized in a mortar toproduce an alloy powder. Thereafter, a crystal structure of theaforementioned alloy powder was analyzed through the XRD measurement inwhich CuKα was set as a radiation source. FIG. 1 illustrates an X-raydiffraction pattern of the magnetic material of an example 1. As aresult of the XRD measurement, it was confirmed that the alloy powderincludes a metal structure having the ThMn₁₂ type crystal phase as itsmain phase. Further, by calculatingI_(α-(Fe, Co))/(I_(α-(Fe, Co))+I_(ThMn12)), a precipitation amount ofthe α-(Fe, Co) phase was evaluated. In addition, by calculatingI₃₋₂₉/(I₃₋₂₉+I_(ThMn2)), a precipitation of the Nd₃(Fe, Ti)₂₉ typecrystal phase was evaluated.

Further, the VSM device was used to evaluate the magnetic physicalproperties of the magnetic material. A magnetic field of 5.0 T wasapplied in an in-plane direction of each of the alloy thin strips, andthe magnetic field was then swept to −5.0 T, thereby measuring amagnetic field H and magnetization M. By applying a saturationasymptotic law expressed by the following formula (1) with respect totetragon, to a relationship between the magnetization M and the magneticfield intensity H during when the applied magnetic field was loweredfrom 5.0 T to 4.5 T, saturation magnetization Ms of the entire magneticmaterial was calculated.M=Ms(1−H _(A) ²/15H ²) (Ms indicates the saturation magnetization, and H_(A) indicates the anisotropic magnetic field.)  (1)

Based on the peak intensity brought by the α-(Fe, Co) phase in the X-raydiffraction pattern, the contribution of the α-(Fe, Co) phase withrespect to the saturation magnetization was evaluated, and this wassubtracted from the saturation magnetization of the entire magneticmaterial, to thereby determine the saturation magnetization of the mainphase. Concretely, a powder sample having no peak intensity brought bythe α-(Fe, Co) phase in the X-ray diffraction pattern was produced, andto the power sample, a powder sample having the α-(Fe, Co) phase wasadded and sufficiently mixed, to thereby produce a plurality of samples.A mass fraction of the powder sample having the α-(Fe, Co) phase in eachof the plurality of samples is different within a range of not less than0 mass % nor more than 21 mass %. When a crystal structure of each ofthe samples was analyzed through the XRD measurement, a ratio betweenthe mass fraction of the powder sample having the α-(Fe, Co) phase and amaximum value of the peak intensityI_(α-(Fe, Co))/(I_(α-(Fe, Co))+I_(ThMn12)) was confirmed to have alinear relationship. Based on this, a mass fraction of the α-(Fe, Co)phase was determined from the peak intensity of the α-(Fe, Co) phase inthe X-ray diffraction pattern, and the mass fraction was converted intothe contribution of the α-(Fe, Co) phase to the saturationmagnetization.

Next, concentrations of elements in the main phase were measured at fivepoints, respectively, in three observation visual fields through theSEM-EDX measurement, and by calculating simple average at 15 pointsabove, the concentration of the element M in the main phase wascalculated. As the measurement point, a point where the α-(Fe, Co) phasedoes not exist within a radius of 5 μm in a SEM image was selected. Inthe SEM observation, the observation was performed at an accelerationvoltage of 30 kV by using SU8020 manufactured by HitachiHigh-Technologies Corporation. Further, in the SEM-EDX measurement, themeasurement was conducted by using Octane-super (semiconductor elementsize: 60 mm²) manufactured by EDAX, with a working distance set to 15 mmand a live time set to 100 seconds. In the calculation of theconcentrations of the elements, only the constituent elements of therespective samples were set as calculation targets, in which Laradiation was applied to Sm, Zr, and Y, and Kα radiation was applied toFe, Co, and Ti.

Examples 39 to 41

Appropriate amounts of raw materials were weighed to produce alloys byusing the arc melting method. Next, each of the alloys was melted, andthe obtained molten metal was subjected to rapid cooling by using thestrip cast method, to thereby produce an alloy thin strip. Theabove-described alloy thin strips were heated for 4 hours at 1100° C.under an Ar atmosphere. Thereafter, each of the alloy thin strips waspulverized in a mortar, and the obtained powder was heated for 4 hoursat 450° C. in a nitrogen gas atmosphere. After that, compositions of thealloy powders were analyzed by using the ICP-AES. The compositions ofthe magnetic materials obtained by using the ICP-AES are presented inTable 1.

Next, a crystal structure of the aforementioned alloy powder wasanalyzed through the XRD measurement in which the CuKα was set as aradiation source. As a result of the XRD measurement, it was confirmedthat the alloy powder includes a metal structure having the ThMn₁₂ typecrystal phase as its main phase. Further, by calculatingI_(α-(Fe, Co))/(I_(α-(Fe, Co))+I_(ThMn12)), a precipitation amount ofthe α-(Fe, Co) phase was evaluated. In addition, by calculatingI₃₋₂₉/(I₃₋₂₉+I_(ThMn12)), a precipitation of the Nd₃(Fe, Ti)₂₉ typecrystal phase was evaluated.

Further, the alloy powder was solidified in an acrylic square-shapedcell by using paraffin, and the VSM was used to evaluate the magneticphysical properties of the magnetic materials. The measurement conditionand the method of calculating the saturation magnetization are similarto those in the examples 1 to 30.

Next, concentrations of respective elements in the main phase weremeasured at five points, respectively, in three observation visualfields through the SEM-EDX measurement, and by calculating simpleaverage at 15 points above, the concentration of the element M in themain phase was calculated.

Examples 42, 43

Appropriate amounts of raw materials were weighed to produce alloys byusing the arc melting method. Next, each of the alloys was melted, andthe obtained molten metal was subjected to rapid cooling by using thestrip cast method, to thereby produce an alloy thin strip. Theabove-described alloy thin strips were heated for 4 hours at 1100° C.under an Ar atmosphere. Thereafter, compositions of the alloy thinstrips after being subjected to the heating were analyzed by using theICP-AES. The compositions of the magnetic materials obtained by usingthe ICP-AES are presented in Table 1.

Next, each of the alloy thin strips was pulverized in a mortar toproduce an alloy powder. Thereafter, a crystal structure of theaforementioned alloy powder was analyzed through the X-ray diffractionmeasurement in which CuKα was set as a radiation source. As a result ofthe XRD measurement, it was confirmed that the alloy powder includes ametal structure having the ThMn₂ type crystal phase as its main phase.Further, by calculating I_(α-(Fe, Co))/(I_(α-(Fe, Co))+I_(ThMn12)), aprecipitation amount of the α-(Fe, Co) phase was evaluated. In addition,by calculating I₃₋₂₉/(I₃₋₂₉+I_(ThMn12)), a precipitation of the Nd₃(Fe,Ti)₂₉ type crystal phase was evaluated.

Further, the VSM was used to evaluate the magnetic physical propertiesof the magnetic materials. The measurement condition and the method ofcalculating the saturation magnetization are similar to those in theexamples 1 to 41.

Next, concentrations of respective elements in the main phase weremeasured at five points, respectively, in three observation visualfields through the SEM-EDX measurement, and by calculating simpleaverage at 15 points above, the concentration of the element M in themain phase was calculated.

Comparative Examples 1 to 5

Appropriate amounts of raw materials were weighed to produce alloys byusing the arc melting method. Next, each of the alloys was heated for 4hours at 1100° C. under an Ar atmosphere, without being subjected tomelting and rapid cooling. Thereafter, compositions of the alloys afterbeing subjected to the heating were analyzed by using the ICP-AES. Thecompositions of the magnetic materials obtained by using the ICP-AES arepresented in Table 1.

Next, each of the alloy thin strips was pulverized in a mortar toproduce an alloy powder. Thereafter, a crystal structure of theaforementioned alloy powder was analyzed through the X-ray diffractionmeasurement in which CuKα was set as a radiation source. FIG. 2illustrates an X-ray diffraction pattern of the magnetic material of thecomparative example 1. As a result of the XRD measurement, it wasconfirmed that the alloy powder includes a metal structure having theThMn₁₂ type crystal phase as its main phase. Further, by calculatingI_(α-(Fe, Co))/(I_(α-(Fe, Co))+I_(ThMn12)), a precipitation amount ofthe α-(Fe, Co) phase was evaluated. In addition, by calculatingI₃₋₂₉/(I₃₋₂₉+I_(ThMn12)), a precipitation of the Nd₃(Fe, Ti)₂₉ typecrystal phase was evaluated.

Further, the VSM was used to evaluate the magnetic physical propertiesof the magnetic materials. The measurement condition and the method ofcalculating the saturation magnetization are similar to those in theexamples 1 to 43.

Next, concentrations of respective elements in the main phase weremeasured at five points, respectively, in three observation visualfields through the SEM-EDX measurement, and by calculating simpleaverage at 15 points above, the concentration of the element M in themain phase was calculated.

TABLE 1 Concen- Satura- tration Satura- tion of tion Magneti- ElementMagneti- Anisotropic zation M in zation Magnetic of Main of Field ofMagnet Phase I_(α-(Fe,) _(Co))/ I₃₋₂₉/ Main Magnet Material (atomic(I_(α(Fe,) _(Co)) + (I₃₋₂₉ + Phase Material Composition of MagnetMaterial (T) percent) I_(ThMn12) I_(ThMn12)) (T) (MA/m) Example 1(Sm_(0.82)Y_(0.18))_(7.7)(Fe_(0.70)Co_(0.30))_(88.4)Ti_(3.9) 1.55 87.80.099 0.025 1.50 6.0 Example 2(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)Nb_(3.6) 1.54 88.00.106 0.029 1.51 5.5 Example 3(Sm_(0.72)Y_(0.28))_(7.5)Fe_(88.5)Ti_(4.0) 1.53 87.8 0.131 0.025 1.497.8 Example 4 (Sm_(0.71)Y_(0.29))_(7.5)Fe_(88.9)Ti_(3.6) 1.52 88.0 0.1430.030 1.48 7.6 Example 5(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)V_(3.6) 1.53 87.60.132 0.031 1.49 5.2 Example 6(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)Ta_(3.6) 1.52 87.70.136 0.031 1.48 5.4 Example 7(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)Mo_(3.6) 1.53 87.60.140 0.031 1.49 5.1 Example 8(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)W_(3.6) 1.52 87.60.139 0.030 1.48 5.3 Example 9(Sm_(0.72)Y_(0.14)Zr_(0.14))_(7.5)(Fe_(0.70)Co_(0.30))_(88.5)Ti_(4.0)1.52 87.6 0.137 0.026 1.48 5.4 Example 10(Sm_(0.71)Y_(0.19)Zr_(0.10))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)Nb_(3.6)1.53 87.7 0.132 0.031 1.49 5.4 Example 11(Sm_(0.71)Y_(0.19)Hf_(0.10))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)Nb_(3.6)1.52 87.6 0.129 0.030 1.48 5.2 Example 12(Sm_(0.71)Y_(0.19)Zr_(0.06)Hf_(0.04))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)Nb_(3.6)1.52 87.7 0.136 0.030 1.48 5.1 Example 13(Sm_(0.72)Y_(0.28))_(7.5)(Fe_(0.70)Co_(0.30))_(88.5)Nb_(2.5)Ti_(1.5)1.54 87.6 0.109 0.025 1.51 5.4 Example 14(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.29)Al_(0.01))_(88.9)Nb_(3.6)1.53 87.6 0.106 0.032 1.50 5.0 Example 15(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.29)Si_(0.01))_(88.9)Nb_(3.6)1.54 87.7 0.107 0.032 1.51 4.9 Example 16(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.29)Cr_(0.01))_(88.9)Nb_(3.6)1.54 87.6 0.105 0.032 1.51 5.0 Example 17(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.29)Mn_(0.01))_(88.9)Nb_(3.6)1.53 87.8 0.106 0.033 1.50 5.0 Example 18(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.29)Ni_(0.01))_(88.9)Nb_(3.6)1.54 87.6 0.107 0.032 1.51 4.8 Example 19(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.29)Cu_(0.01))_(88.9)Nb_(3.6)1.53 87.9 0.108 0.033 1.50 4.9 Example 20(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.29)Ga_(0.01))_(88.9)Nb_(3.6)1.54 87.6 0.106 0.033 1.51 5.0 Example 21(Sm_(0.75)Y_(0.25))_(7.6)(Fe_(0.80)Co_(0.20))_(88.5)Ti_(3.9) 1.55 88.30.066 0.025 1.53 6.7 Example 22(Sm_(0.83)Y_(0.17))_(7.6)(Fe_(0.82)Co_(0.18))_(88.8)Nb_(3.6) 1.52 87.50.131 0.028 1.48 7.5 Example 23(Sm_(0.81)Y_(0.19))_(7.5)(Fe_(0.85)Co_(0.15))_(88.5)Ti_(4.0) 1.52 88.10.074 0.024 1.50 7.4 Example 24(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.90)Co_(0.10))_(88.5)Ti_(4.0) 1.50 87.90.077 0.024 1.48 7.4 Example 25(Sm_(0.85)Y_(0.15))_(7.5)(Fe_(0.79)Co_(0.21))_(88.5)Ti_(4.0) 1.55 88.20.072 0.025 1.53 7.4 Example 26(Sm_(0.58)Y_(0.42))_(7.5)(Fe_(0.80)Co_(0.20))_(88.6)Ti_(3.9) 1.52 88.00.071 0.025 1.50 6.0 Example 27(Sm_(0.71)Y_(0.29))_(7.7)(Fe_(0.60)Co_(0.40))_(88.7)Ti_(3.6) 1.54 87.60.108 0.034 1.51 4.5 Example 28(Sm_(0.75)Y_(0.25))_(7.8)(Fe_(0.80)Co_(0.20))_(89.2)Ti_(3.0) 1.52 86.80.197 0.060 1.46 6.3 Example 29(Sm_(0.93)Y_(0.07))_(7.7)(Fe_(0.85)Co_(0.15))_(88.7)Ti_(3.6) 1.50 86.30.201 0.036 1.44 7.5 Example 30(Sm_(0.90)Y_(0.07))_(7.7)(Fe_(0.48)Co_(0.52))_(88.7)Ti_(3.6) 1.49 86.70.199 0.040 1.43 3.5 Example 31(Sm_(0.6)Y_(0.4))_(7.8)(Fe_(0.80)Co_(0.20))_(88.6)Ti_(3.6) 1.58 88.30.080 0.025 1.56 5.8 Example 32(Sm_(0.65)Y_(0.35))_(7.8)(Fe_(0.80)Co_(0.20))_(88.9)Ti_(3.3) 1.56 88.10.092 0.027 1.54 6.1 Example 33(Sm_(0.55)Y_(0.45))_(7.8)(Fe_(0.80)Co_(0.20))_(88.8)Ti_(3.4) 1.57 88.00.082 0.030 1.55 5.3 Example 34(Sm_(0.6)Y_(0.4))_(7.8)(Fe_(0.80)Co_(0.20))_(88.6)Nb_(3.6) 1.56 88.20.075 0.024 1.55 5.9 Example 35(Sm_(0.65)Y_(0.35))_(7.8)(Fe_(0.80)Co_(0.20))_(88.9)Nb_(3.3) 1.54 88.10.081 0.026 1.52 5.5 Example 36(Sm_(0.55)Y_(0.45))_(7.8)(Fe_(0.80)Co_(0.20))_(88.8)Nb_(3.4) 1.55 88.30.078 0.028 1.54 5.3 Example 37(Sm_(0.4)Y_(0.6))_(7.8)(Fe_(0.80)Co_(0.20))_(88.7)Ti_(3.5) 1.55 88.20.078 0.027 1.54 4.7 Example 38(Sm_(0.6)Y_(0.4))_(7.8)(Fe_(0.80)Co_(0.20))_(89.7)Ti_(2.5) 1.42 86.70.201 0.070 1.38 4.0 Example 39(Nd_(0.72)Y_(0.28))_(7.2)(Fe_(0.70)Co_(0.30))_(81.9)Ti_(3.8)N_(7.1) 1.5287.7 0.138 0.025 1.48 6.5 Example 40(Nd_(0.72)Y_(0.28))_(7.5)(Fe_(0.70)Co_(0.30))_(82.2)Nb_(3.5)N_(6.8) 1.5387.8 0.123 0.027 1.49 6.7 Example 41(Sm_(3.65)Nd_(0.1)Y_(0.25))_(7.4)(Fe_(0.79)Co_(0.21))_(82.4)Nb_(3.9)N_(6.3)1.52 87.7 0.112 0.026 1.49 6.2 Example 42(Sm_(0.72)Y_(0.28))_(7.5)(Fe_(0.70)Co_(0.30))_(88.5)Ti_(4.0) 1.47 85.90.213 0.025 1.40 5.4 Example 43(Sm_(0.71)Y_(0.29))_(7.5)(Fe_(0.70)Co_(0.30))_(88.0)Nb_(3.6) 1.46 86.10.204 0.029 1.40 5.3 Comp.(Sm_(0.68)Zr_(0.32))_(7.8)(Fe_(0.70)Co_(0.30))_(88.2)Ti_(4.0) 1.48 86.50.242 0.025 1.40 5.5 Exam 1 Comp.(Sm_(0.64)Zr_(0.36))_(7.7)(Fe_(0.69)Co_(0.31))_(88.4)Nb_(3.9) 1.47 85.50.251 0.025 1.39 5.6 Exam 2 Comp.(Sm_(0.10)Y_(0.90))_(7.5)(Fe_(0.70)Co_(0.30))_(88.5)Ti_(4.0) 1.43 86.40.221 0.025 1.36 3.0 Exam 3 Comp.(Sm_(0.12)Y_(0.88))_(7.5)(Fe_(0.70)Co_(0.30))_(88.9)Nb_(3.6) 1.48 86.30.235 0.025 1.41 3.1 Exam 4 Comp.(Sm_(0.9)Y_(0.1))_(7.8)(Fe_(0.25)Co_(0.75))_(89.3)Ti_(2.9) 1.27 86.10.211 0.070 1.20 1.2 Exam 5

Table 1 shows that 30 atomic percent or more of the element M in each ofthe magnetic materials of examples 1 to 43 is Fe, and each of thematerials has high saturation magnetization. The concentration of theelement M in the main phase in each of the magnetic materials ofexamples 1 to 27, 31 to 37, and 39 to 41 is 87.4 atomic percent or moreof the total amount of the element R, the element Y, the element M, andthe element T, and thereby each of the materials has higher saturationmagnetization. When the element M in each of the magnetic materials ofexamples 21 to 26, 28, 29, 31 to 38, and 41 is expressed byFe_(1-y)Co_(y), the value of the y is 0.01 or more and 0.3 or less, eachof the materials has higher anisotropic magnetic field. Further,I_(α(Fe, Co))/(I_(α-(Fe, Co))+I_(ThMn12)) of the magnetic material ineach of the examples 1 to 27, 31 to 37, and 39 to 41 is less than 0.15.I₃₋₂₉/(I₃₋₂₉+I_(ThMn12)) of the magnetic material in each of theexamples 31 to 37 is less than 0.020 and the saturation magnetization ofthe main phase thereof is 1.52 T or more. Furthermore, the saturationmagnetization of the main phase of the magnetic material in each of theexamples 1 to 27, 31 to 37, and 39 to 41 is 1.48 T or more, and theanisotropic magnetic field in each of the examples 1 to 43 is 3 MA/m ormore.

In contract, less than 30 atomic percent of the element M in each of themagnetic materials of comparative examples 5 is Fe, and each of thematerials has low saturation magnetization and low anisotropic magneticfield. The concentration of the element Y in each of the comparativeexamples 1 to 4 is outside the scope of the inventions, and theprecipitation amount of the α-(Fe, Co) phase of the magnetic material ineach of the comparative examples 1 to 4 is larger than the precipitationamount of the α-(Fe, Co) phase of the magnetic material in each of theexamples 1 to 43.

Both of the values of the saturation magnetization and the values of theanisotropic magnetic field in the examples 1 to 43 and the comparativeexamples 1 to 5 is determined in accordance with magnetic field used forthe evaluation thereof.

The above-described embodiments have been presented by way of exampleonly, and are not intended to limit the scope of the inventions. Indeed,the novel embodiments described herein may be embodied in a variety ofother forms; furthermore, various omissions, substitutions and changesmay be made without departing from the spirit of the inventions. Theseembodiments and their modifications fall within the scope and spirit ofthe inventions and fall within the scope of the inventions described inclaims and their equivalents.

What is claimed is:
 1. A magnetic material expressed by a composition formula: (R_(1-x)Y_(x))_(a)M_(b)T_(c)A_(d) where R is at least one element selected from the group consisting of rare-earth elements, T is at least one element selected from the group consisting of Ti, V, Nb, Ta, Mo, and W, M is Fe or Fe and Co, A is at least one element selected from the group consisting of N, C, B, H, and P, x is a number satisfying 0.3<x≤0.6, a is a number satisfying 4≤a≤20 atomic percent, c is a number satisfying 3<c≤3.8 atomic percent, b is a number satisfying b=100−a−c−d atomic percent, and d is a number satisfying 0≤d≤18 atomic percent, the magnetic material comprising: a main phase consisting of a ThMn₂ type crystal phase, wherein 30 atomic percent or more of the element M in the composition formula is Fe.
 2. The magnetic material according to claim 1, wherein in an X-ray diffraction pattern of the magnetic material, a ratio of a maximum value of a peak intensity corresponding to a Nd₃(Fe, Ti)₂₉ type crystal phase to a sum of a maximum value of a peak intensity corresponding to the ThMn₁₂ type crystal phase and the maximum value of the peak intensity corresponding to the Nd₃(Fe, Ti)₂₉ type crystal phase is less than 0.04.
 3. The magnetic material according to claim 1, wherein the d is a number satisfying d=0 atomic percent, wherein 50 atomic percent or more of the element R in the composition formula is Sm.
 4. The magnetic material according to claim 1, wherein the d is a number satisfying 0<d≤18 atomic percent, wherein 50 atomic percent or more of the element R in the composition formula is at least one element selected from the group consisting of Ce, Pr, Nd, Tb, and Dy.
 5. The magnetic material according to claim 1, wherein in an X-ray diffraction pattern of the magnetic material, a ratio of a maximum value of a peak intensity corresponding to an α-(Fe, Co) phase to a sum of a maximum value of a peak intensity corresponding to the ThMn₁₂ type crystal phase and the maximum value of the peak intensity corresponding to the α-(Fe, Co) phase is less than 0.20.
 6. The magnetic material according to claim 1, wherein 50 atomic percent or less of the element Y in the composition formula is replaced with at least one element selected from the group consisting of Zr and Hf.
 7. The magnetic material according to claim 1, wherein 50 atomic percent or more of the element T in the composition formula is Ti or Nb.
 8. The magnetic material according to claim 1, wherein 20 atomic percent or less of the element M in the composition formula is replaced with at least one element selected from the group consisting of Al, Si, Cr, Mn, Ni, Cu, and Ga.
 9. The magnetic material according to claim 1, wherein a concentration of the element M in the main phase is 87.4 atomic percent or more of a total amount of the element R, the element Y, the element M, and the element T in the main phase.
 10. The magnetic material according to claim 1, wherein the M in the composition formula is expressed by Fe_(1-y)Co_(y), wherein the y is a number satisfying 0.01≤y≤0.3.
 11. A permanent magnet comprising the magnetic material according to claim
 1. 12. A permanent magnet comprising a sintered body of the magnetic material according to claim
 1. 13. A rotary electrical machine, comprising: a stator; and a rotor, wherein the stator or the rotor comprises the permanent magnet according to claim
 12. 14. The rotary electrical machine according to claim 13, wherein the rotor is connected to a turbine via a shaft.
 15. A vehicle, comprising the rotary electrical machine according to claim
 13. 16. The vehicle according to claim 15, wherein: the rotor is connected to a shaft; and rotation is transmitted to the shaft. 